US6918968B2 - Austenitic stainless steel - Google Patents
Austenitic stainless steel Download PDFInfo
- Publication number
- US6918968B2 US6918968B2 US10/829,274 US82927404A US6918968B2 US 6918968 B2 US6918968 B2 US 6918968B2 US 82927404 A US82927404 A US 82927404A US 6918968 B2 US6918968 B2 US 6918968B2
- Authority
- US
- United States
- Prior art keywords
- content
- steel
- less
- austenitic stainless
- high temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 27
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 27
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 20
- 229910052802 copper Inorganic materials 0.000 claims abstract description 16
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 16
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 16
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 14
- 239000012535 impurity Substances 0.000 claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 10
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 10
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 9
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 9
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 9
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 9
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 239000001301 oxygen Substances 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 7
- 229910052741 iridium Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052763 palladium Inorganic materials 0.000 claims abstract description 7
- 229910052697 platinum Inorganic materials 0.000 claims abstract description 7
- 229910052706 scandium Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052709 silver Inorganic materials 0.000 claims abstract description 7
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 6
- 229910052702 rhenium Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 5
- 229910000831 Steel Inorganic materials 0.000 description 112
- 239000010959 steel Substances 0.000 description 112
- 239000010949 copper Substances 0.000 description 34
- 239000010955 niobium Substances 0.000 description 31
- 230000000694 effects Effects 0.000 description 25
- 239000011651 chromium Substances 0.000 description 24
- 239000002244 precipitate Substances 0.000 description 21
- 239000000126 substance Substances 0.000 description 17
- 230000000052 comparative effect Effects 0.000 description 15
- 239000000203 mixture Substances 0.000 description 15
- 238000010438 heat treatment Methods 0.000 description 14
- 238000001556 precipitation Methods 0.000 description 13
- 239000011572 manganese Substances 0.000 description 12
- 229910001566 austenite Inorganic materials 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 150000004767 nitrides Chemical class 0.000 description 10
- 230000007423 decrease Effects 0.000 description 9
- 239000011777 magnesium Substances 0.000 description 9
- 239000011575 calcium Substances 0.000 description 8
- 230000006872 improvement Effects 0.000 description 8
- 230000003647 oxidation Effects 0.000 description 8
- 238000007254 oxidation reaction Methods 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
- 239000010936 titanium Substances 0.000 description 8
- 238000005275 alloying Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000001771 impaired effect Effects 0.000 description 7
- 238000005482 strain hardening Methods 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 230000009467 reduction Effects 0.000 description 6
- 230000003247 decreasing effect Effects 0.000 description 5
- 230000002708 enhancing effect Effects 0.000 description 5
- 229910000765 intermetallic Inorganic materials 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 229910001220 stainless steel Inorganic materials 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- TZCXTZWJZNENPQ-UHFFFAOYSA-L barium sulfate Chemical compound [Ba+2].[O-]S([O-])(=O)=O TZCXTZWJZNENPQ-UHFFFAOYSA-L 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000001192 hot extrusion Methods 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 230000005540 biological transmission Effects 0.000 description 2
- 125000004432 carbon atom Chemical group C* 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical compound O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 2
- 238000010894 electron beam technology Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 125000004433 nitrogen atom Chemical group N* 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 230000001629 suppression Effects 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 125000004429 atom Chemical group 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical group [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 238000005034 decoration Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- WUAPFZMCVAUBPE-UHFFFAOYSA-N rhenium atom Chemical compound [Re] WUAPFZMCVAUBPE-UHFFFAOYSA-N 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical group [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical group [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B42—BOOKBINDING; ALBUMS; FILES; SPECIAL PRINTED MATTER
- B42D—BOOKS; BOOK COVERS; LOOSE LEAVES; PRINTED MATTER CHARACTERISED BY IDENTIFICATION OR SECURITY FEATURES; PRINTED MATTER OF SPECIAL FORMAT OR STYLE NOT OTHERWISE PROVIDED FOR; DEVICES FOR USE THEREWITH AND NOT OTHERWISE PROVIDED FOR; MOVABLE-STRIP WRITING OR READING APPARATUS
- B42D3/00—Book covers
- B42D3/04—Book covers loose
- B42D3/045—Protective cases for books
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B42—BOOKBINDING; ALBUMS; FILES; SPECIAL PRINTED MATTER
- B42D—BOOKS; BOOK COVERS; LOOSE LEAVES; PRINTED MATTER CHARACTERISED BY IDENTIFICATION OR SECURITY FEATURES; PRINTED MATTER OF SPECIAL FORMAT OR STYLE NOT OTHERWISE PROVIDED FOR; DEVICES FOR USE THEREWITH AND NOT OTHERWISE PROVIDED FOR; MOVABLE-STRIP WRITING OR READING APPARATUS
- B42D1/00—Books or other bound products
- B42D1/06—Books or other bound products in which the fillings and covers are united by other means
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B42—BOOKBINDING; ALBUMS; FILES; SPECIAL PRINTED MATTER
- B42D—BOOKS; BOOK COVERS; LOOSE LEAVES; PRINTED MATTER CHARACTERISED BY IDENTIFICATION OR SECURITY FEATURES; PRINTED MATTER OF SPECIAL FORMAT OR STYLE NOT OTHERWISE PROVIDED FOR; DEVICES FOR USE THEREWITH AND NOT OTHERWISE PROVIDED FOR; MOVABLE-STRIP WRITING OR READING APPARATUS
- B42D3/00—Book covers
- B42D3/10—Book covers with locks or closures
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B42—BOOKBINDING; ALBUMS; FILES; SPECIAL PRINTED MATTER
- B42P—INDEXING SCHEME RELATING TO BOOKS, FILING APPLIANCES OR THE LIKE
- B42P2241/00—Parts, details or accessories for books or filing appliances
- B42P2241/02—Fasteners; Closures
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
- F28F21/081—Heat exchange elements made from metals or metal alloys
- F28F21/082—Heat exchange elements made from metals or metal alloys from steel or ferrous alloys
- F28F21/083—Heat exchange elements made from metals or metal alloys from steel or ferrous alloys from stainless steel
Definitions
- the present invention relates to an austenitic stainless steel, which is used as heat-resistant and pressure-resistant members, such as tubes, plates, bars, and forged parts for power generating boilers, chemical plants and the like.
- the invention relates specifically to an austenitic stainless steel, excellent in creep strength, creep rupture ductility and hot workability.
- 18-8 austenitic stainless steels such as SUS304H, SUS316H, SUS321H and SUS347H.
- SUS304H, SUS316H, SUS321H and SUS347H As materials of devices, which are used for boilers, chemical plants and the like, under a high temperature environment, 18-8 austenitic stainless steels such as SUS304H, SUS316H, SUS321H and SUS347H, have been used.
- the use conditions of these devices under such a high temperature environment have become remarkably severe. Accordingly the required properties for the materials used in such an environment have attained a higher level.
- the conventional 18-8 austenitic stainless steels are insufficient in high temperature strength, particularly in creep strength, so in these circumstances, an austenitic stainless steel, having improved high temperature strength by adding the particular amounts of various elements, has been proposed.
- an austenitic stainless steel in which high temperature strength was significantly improved by adding the comparatively inexpensive Cu together with Nb and N in proper amounts has been proposed in Publication of examined Patent Application No. Hei 8-30247, Publication of unexamined Patent, Application No. Hei 7-138708 and Publication of unexamined Patent Application No. Hei 8-13102.
- Cu precipitates coherently with the austenite matrix during use at high temperatures, and Nb precipitates as complex nitiride with Cr, NbCrN. Since these precipitates very effectively act as barriers against the dislocation movement, the high temperature strength of the austenitic stainless steel is enhanced.
- the austenitic stainless steels proposed in the above-mentioned Patent Documents will be insufficient in various properties.
- the above-mentioned Cu, Nb and N added steels, as materials for being able to endure in the said environment of high temperature and high pressure are still insufficient in high temperature strength and corrosion resistance.
- the toughness of the steel, after being used at high temperatures of 800° C. or higher for long period is insufficient.
- the hot workability of the Cu, Nb and N added steels is inferior to that of the conventional 18-8 austenitic stainless steel, therefore an prompt improvement of the steels is required.
- a material having poor hot workability is formed into a seamless tube by hot extrusion. Since the internal temperature of the material becomes higher than the heating temperature, due to the heat produced by working, material having insufficient workability at 1200° C. or higher generates cracks, so-called lamination, and inner defects. This phenomenon is the same as in a piercing by the piercer in the Mannesmann mandrel mill process and the like.
- the present invention has been invented for solving the above-mentioned problems.
- the objective of the present invention is to provide an austenitic stainless steel in which the creep strength and creep rupture ductility are improved, and the hot workability, particularly the high temperature ductility at 1200° C. or higher, is significantly improved.
- the inventors have studied in order to attain the above-mentioned objective and found the following.
- the present invention has been completed based on the above-mentioned findings, and the gist of the present invention is the following austenitic stainless steels.
- An austenitic stainless steel characterized by consisting of, by mass %, C: more than 0.05% to 0.15%, Si: 2% or less, Mn: 0.1 to 3%, P: 0.04% or less, S: 0.01% or less, Cr: more than 20% to less than 28%, Ni: more than 15% to 55%, Cu: more than 2% to 6%, Nb: 0.1 to 0.8%, V: 0.02 to 1.5%, sol. Al: 0.001 to 0.1%, N: more than 0.05% to 0.3% and O (Oxygen): 0.006% or less, and the balance Fe and impurities, further characterized by satisfying the following formulas (1) and (2). Wherein each element symbol in the formulas (1) and (2) represents the content (mass %) of each element: P ⁇ 1/(11 ⁇ Cu) (1) sol.Al ⁇ 0.4 ⁇ N (2)
- the above-mentioned austenitic stainless steel may contain, instead of a part of Fe, at least one element selected from the first element group consisting of Co: 0.05 to 5%, Mo: 0.05 to 5%, W: 0.05 to 10%, Ti: 0.002 to 0.2%, B: 0.0005 to 0.05%, Zr: 0.0005 to 0.2%, Hf: 0.0005 to 1%, Ta: 0.01 to 8%, Re: 0.01 to 8%, Ir: 0.01 to 5%, Pd: 0.01 to 5%, Pt: 0.01 to 5% and Ag: 0.01 to 5%, and/or at least one element selected from the second element group consisting of Mg: 0.0005 to 0.05%, Ca: 0.0005 to 0.05%, Y: 0.0005 to 0.5%, La: 0.0005 to 0.5%, Ce: 0.0005 to 0.5%, Nd: 0.0005 to 0.5% and Sc: 0.0005 to 0.5%.
- Mo and W are contained, the following formula (3) should be satisfied. Mo+(W
- the steel according to the present invention satisfies the following formula (4). O ⁇ 1/(60 ⁇ Cu) (4)
- C Carbon
- Carbon is an effective and important alloying element. It is necessary for ensuring tensile strength and creep strength that are required when the steel is used in a high temperature environment. When the carbon content is 0.05% or less, these effects are not sufficient. On the other hand, when the carbon exceeds 0.15%, an amount of unsolved carbide in the solution-treated state increases. The unsolved carbide does not contribute to the improvement of the high temperature strength. Additionally, the excessive amount of carbon deteriorates the mechanical properties such as toughness and weldability. Thus, the C content is set at more than 0.05% but not more than 0.15%. The C content is more preferably 0.13% or less, and most preferably 0.11% or less.
- Si Si (Silicon) is added as a deoxidizer, and is an effective element to enhance oxidation resistance, steam oxidation resistance and the like of the steel. Si, exceeding 2%, promotes the precipitation of intermetallic compounds such as a phase and also the precipitation of a large amount of nitride, and further deteriorates the stability of the structure at high temperatures. Thus the toughness and ductility of the steel are decreased. Further, the weldability and hot workability are also reduced. Accordingly, the Si content is set at 2% or less. When the toughness and ductility are particularly important, the Si content is preferably 1% or less, and more preferably 0.5% or less. When deoxidation is ensured sufficiently by other elements, Si is not necessarily added. However, if the deoxidation of the steel, oxidation resistance, or steam oxidation resistance and the like are essential, the Si content is preferably 0.05% or more. The most preferable Si content is 0.1% or more.
- Mn (Manganese), likewise to Si, has a deoxidizing effect of the molten steel, and fixes S, which is inevitably contained in the steel, as a sulfide to improve hot workability. Mn content of 0.1% or more is needed in order to obtain these effects sufficiently. However, if the Mn content exceeds 3%, the precipitation of intermetallic compound phases such as a phase is promoted so that the stability of structure, high temperature strength and mechanical strength of the steel are deteriorated. Thus, the Mn content is set at 0.1 to 3%. A more preferable Mn content is 0.2 to 2%, and the most preferable Mn content is 0.2 to 1.5%.
- P Phosphorus
- the P content is limited to 0.04% or less. Since P decreases creep rupture ductility, particularly the high temperature ductility at 1200° C. or higher, and the hot workability, due to an interaction with Cu, it is necessary that the P content should be in a range satisfying the following formula (1) in relation to the Cu content. P ⁇ 1/(11 ⁇ Cu) (1)
- S sulfur
- the hot workability is improved by controlling the P content or the O (Oxygen) content properly in accordance with Cu content. Therefore the S content of up to 0.01% is allowable.
- the S content should desirably be 0.005% or less, and even more desirably at 0.003% or less.
- Cr Chromium
- Cr is an important alloying element, which ensures oxidation resistance, steam oxidation resistance, high temperature corrosion resistance and the like. Cr is also an element that forms Cr carbonitride and increases strength. Since, the conventional 18-8 austenitic stainless steel is insufficient in order to exert corrosion resistance and high temperature strength, which is needed under the high temperature environment of 650 to 700° C. or higher, the steel of the present invention needs the addition of more than 20% Cr. The more the Cr content, the more corrosion resistance improves. However, a Cr content of 28% or more makes the austenite structure unstable and facilitates the generation of intermetallic compounds such as the ⁇ phase and an the ⁇ —Cr phase, which reduce the toughness and the high temperature strength of the steel. Accordingly, the Cr content is set at more than 20% to less than 28%.
- Ni Ni (Nickel) is an indispensable alloying element, which ensures the stable austenite structure.
- the most suitable Ni content is determined by the contents of the ferrite stabilizing elements such as Cr, Mo, W and Nb, and the austenite stabilizing elements such as C and N.
- the ferrite stabilizing elements such as Cr, Mo, W and Nb
- the austenite stabilizing elements such as C and N.
- more than 20% Cr must be contained. If the Ni content is 15% or less with respect to this Cr content, it is difficult to make the structure of the steel the single phase of austenite. Further, in this case, an austenite structure becomes unstable during a long period of use, whereby brittle phases such as ⁇ phase precipitate.
- Ni content exceeds 55%, the effects are saturated and the production cost increases.
- the Ni content is set at more than 15% to 55%.
- Cu Copper
- Cu is one of the most important and distinctive elements because it precipitates coherently with the austenite matrix as Cu-phase, during the use at high temperatures, and it significantly enhances creep strength of the steel.
- a Cu content of more than 2% is necessary.
- the Cu content is set from more than 2% to 6%.
- a preferable range of the Cu content is 2.5 to 4%.
- Nb (Niobium) is an important element, similar to Cu and N.
- Nb forms fine carbonitride such as NbCrN, and enhances creep rupture strength and also suppresses grain-coarsening during the solution heat treatment after the final working. Thereby Nb contributes to the improvement of creep rupture ductility.
- the Nb content is less than 0.1%, sufficient effects cannot be obtained.
- the Nb content exceeds 0.8%, in addition to the deterioration of weldability and mechanical properties due to an increase in the unsolved nitride, hot workability, and also particularly high temperature ductility at 1200° C. or higher, is remarkably decreased.
- the Nb content is set at 0.1 to 0.8%.
- a preferable range of the Nb content is 0.2 to 0.6%.
- V (Vanadium) forms carbonitrides such as (Nb,V)CrN, V(C,N), and is known as an effective alloying element for enhancing high temperature strength and creep strength.
- V is added for enhancing the high temperature strength and toughness during long period of use at high temperatures, particularly at 800° C. or higher.
- the high temperature and toughness enhancement effects of V is based on the fact that V contributes to the promotion of precipitation of fine Cu-phase, the suppression of grain coarsening and the suppression of coarsening of M 23 C 6 , on grain boundaries. Further V precipitates as V(C,N) thereby increases the rate of grain boundary decoration by precipitates.
- V content is set at 0.02 to 1.5%.
- a preferable range of the V content is 0.04 to 1%.
- Sol. Al (acid soluble Aluminum) is an element added as a deoxidizer in molten steel. It is important that its content must be severely controlled in accordance with the N content in the steel of the present invention. Sol.Al content of 0.001% or more is necessary in order to obtain the effects. However, if the sol.Al content exceeds 0.1%, the precipitation of intermetallic compounds such as the ⁇ phase is promoted during the use at high temperatures and thereby decreasing toughness, ductility and high temperature strength. Thus, the sol.Al content is set at 0.001 to 0.1%. A preferable range of the sol.Al content is 0.005 to 0.05%, and the most desirable range is 0.01 to 0.03%.
- sol.Al content of sol.Al must be controlled so as to satisfy the following formula (2) in accordance with the N content. Satisfying the formula (2) prevents N from being consumed uselessly as AlN, which does not contribute to high temperature strength, and, thereby, sufficient amount of precipitation of complex nitiride with Cr, (Nb,V)CrN, which is effective in enhancement of high temperature strength, can be obtained. sol.Al ⁇ 0.4 ⁇ N (2)
- N is an effective alloying element, which ensures the stability of austenite in place of a part of expensive Ni. It is also effective in contributing to enhance tensile strength because it contributes to solid-solution strengthening as an interstitial solid solution element. Also N is an element, which forms fine nitrides such as NbCrN and these nitrides enhance creep strength and creep rupture ductility by suppressing grain coarsening. Therefore, N is one of indispensable and the most important elements similar to Cu and Nb. N content of more than 0.05% is necessary in order to exert these positive effects. However, even if the N content exceeds 0.3%, unsolved nitride increases and a large amount of nitride increases during use at high temperatures. Accordingly, ductility, toughness and weldability are impaired. Thus, the N content is limited in the range of more than 0.05% to 0.3%. A more preferable range is 0.06 to 0.27%.
- O Oxygen
- Oxygen is an element, which is incidentally contained in steel, and remarkably decreases hot workability.
- creep rupture ductility and hot workability especially high temperature ductility at 1200° C. or higher, are further decreased by mutual action of O and Cu.
- One of the austenitic stainless steels of the present invention is the steel, which contains the above-mentioned elements and the balance of Fe and impurities.
- Another austenitic stainless steel of the present invention is a steel containing, in place of a part of Fe, at least one element selected from the first group consisting of Co: 0.05 to 5%, Mo: 0.05 to 5%, W: 0.05 to 10%, Ti: 0.002 to 0.2%, B: 0.0005 to 0.05%, Zr: 0.0005 to 0.2%, Hf: 0.0005 to 1%, Ta: 0.01 to 8%, Re: 0.01 to 8%, Ir: 0.01 to 5%, Pd: 0.01 to 5%, Pt: 0.01 to 5% and Ag: 0.01 to 5%.
- This steel, containing the element(s) belonging to the first group is a steel that has further excellence in high temperature strength. The grounds for selecting the content ranges of these elements will be described below.
- Co Cobalt
- Ni Ni
- the Co content is preferably 0.05 to 5%.
- Mo Mo
- W Tin
- Ti is an alloying element, which forms carbonitride that contributes to enhancing high temperature strength, it may be contained in the steel of the present invention. The effects become significant when the Ti content is 0.002% or more. However, if the Ti content is excessive, mechanical properties may be decreased due to unsolved nitride, and high temperature strength may be reduced due to decrease of fine nitride. Thus the Ti content is desirably 0.002 to 0.2%.
- B (Boron) is contained in carbonitride and also exists on grain boundaries as free B. Since B promotes fine precipitation of carbonitride during the use of the steel at high temperatures and suppresses grain boundary slip through the strengthening of grain boundaries, it improves high temperature strength and creep strength. These effects are remarkable when B content is 0.0005% or more. However, if the B content exceeds 0.05%, weldability deteriorates. Thus the B content is preferably 0.0005 to 0.05%, and a more preferable range of the B content is 0.001 to 0.01%. The most preferable range of the B content is 0.001 to 0.005%.
- Zr Zirconium
- Zrconium is an alloying element, which effects the contribution to grain boundary strengthening in order to enhance high temperature and creep strength, and fixing S to improve hot workability. These effects become remarkable if the Zr content is 0.0005% or more. However, if the Zr content exceeds 0.2%, the mechanical properties such as ductility and toughness are deteriorated. Thus, a preferable range of Zr content is 0.0005 to 0.2%, and more preferable range is 0.01 to 0.1%. The most preferable range is 0.01 to 0.05%.
- Hf (Hafnium) is an element, which contributes mainly to grain boundary strengthening to enhance creep strength. This effect is remarkable when the Hf content is 0.005% or more. However, if the Hf content exceeds 1%, workability and weldability of the steel are impaired. Thus the Hf content is preferably 0.005 to 1%. A more preferable range is 0.01 to 0.8%, and the most preferable range is 0.02 to 0.5%.
- Ta (Tantalum) forms carbonitride, and also is a solid-solution strengthening element. It enhances high temperature strength and creep strength, and this effect is remarkable if the Ta content is 0.01% or more. However, if the Hf content exceeds 8%, workability and mechanical properties of the steel are impaired, thus the Ta content is preferably 0.01 to 8%. A more preferable range of the Ta content is 0.1 to 7%, and the most preferable range is 0.5 to 6%.
- Re (Rhenium) enhances high temperature strength and creep strength mainly as a solid-solution strengthening element. This effect is remarkable if its content is 0.01% or more. However, if the Re content exceeds 8%, the workability and mechanical properties of the steel are impaired. Thus the Re content is preferably 0.01 to 8%. A more preferable range is 0.1 to 7%, and the most preferable range is 0.5 to 6%.
- Ir, Pd, Pt and Ag dissolve in the austenite matrix of the steel to contribute to solid-solution strengthening, and change the lattice constant of the austenite matrix to enhance the long time stability of the Cu-phase, which coherently precipitates with the matrix of the steel. Further, a part of these elements forms fine intermetallic compounds in accordance with its additional amount and enhances high temperature strength and creep strength. These effects are remarkable if their contents are 0.01% or more. However, if the contents exceed 5%, the workability and mechanical properties of the steel are impaired. Thus their contents are preferably 0.01 to 5%. More preferable ranges of their contents are 0.05 to 4%, and the most preferable ranges are 0.1 to 3%.
- Another austenitic stainless steel of the present invention contains, in the place of a part of Fe of the above-mentioned chemical composition, at least one element selected from the second group, consisting of Mg: 0.0005 to 0.05%, Ca: 0.0005 to 0.05%, Y: 0.0005 to 0.5%, La: 0.0005 to 0.5%, Ce: 0.0005 to 0.5%, Nd: 0.0005 to 0.5% and Sc: 0.0005 to 0.5%.
- This steel, containing the second element group element(s) is more excellent in hot workability. The grounds for restricting content ranges of these elements will be described below.
- Mg 0.0005 to 0.05%
- Ca 0.0005 to 0.05%
- the above-mentioned effects are remarkable if the content is 0.0005% or more respectively. However, if the content exceeds 0.05%, the steel quality is impaired and hot workability and ductility decrease.
- the content of each 0.0005 to 0.05% is preferable, and a more preferable range is 0.001 to 0.02%. The most preferable range is 0.001 to 0.01%.
- All of Y, La, Ce, Nd and Sc are elements that fix S as a sulfide and improve hot workability. They also improve the adhesion of the Cr 2 O 3 protective film on the steel surface, and particularly improve the oxidation resistance when the steel suffers repeated oxidation. Further, since these elements contribute to grain boundary strengthening, they enhance creep rupture strength and creep rupture ductility. When the content is 0.0005% or more respectively, the above-mentioned effects become remarkable. However, if the content exceeds 0.5%, a large amount of inclusions such as oxide are produced and workability and weldability are impaired. Accordingly, the content of 0.0005 to 0.05% is preferable, and a more referable range is 0.001 to 0.03%. The most preferable range is 0.002 to 0.15%.
- the steels of the present invention in which the above-mentioned chemical compositions are specified, can be widely applied to use where high temperature strength and corrosion resistance are needed.
- These products may be steel tube, steel plate, steel bar, forged steel products and the like.
- the diameter of the precipitates of V(C,N) carbonitride is preferably 50 nm or less.
- the (Nb,V)CrN is a kind of complex nitiride with Cr called as a “Z-phase”, and its crystal structure is tetragonal.
- (Nb,V), Cr and N exist at a ratio of 1:1:1 in a unit cell of the (Nb,V)CrN complex nitiride with Cr.
- the V(C,N) carbonitride is formed as the NaCl-type cubic carbide (VC) or the cubic nitride (VN), or a cubic carbonitride in which a part of the C atoms and the N atoms are mutually substituted.
- These carbides and nitrides form a face-centered cubic lattice in which metal atoms are densely stacked and have a crystal structure in which the octahedral sites are occupied by a C atom or a N atom.
- the amount of these precipitates can be measured by use of a transmission electron microscope of a magnification of 10,000 or more while observing the structure of the steel.
- the measurement may be made by countering the respective precipitates separated by an electron beam diffraction pattern.
- the observation is desirably carried out in five fields.
- the following method is recommendable for manufacturing the steel according to the present invention.
- Billets are prepared by casting or by “casting and forging” or “casting and rolling” of the steel having the above-mentioned chemical composition.
- the billets are hot-worked in, for example, a hot extrusion or a hot rolling process. It is desirable that the heating temperature before hot working is 1160° C. to 1250° C.
- the finishing temperature of the hot working is desirably not lower than 1150° C. It is preferable to cool the hot worked products at a large cooling rate of 0.25° C./sec or more, to at least a temperature of not higher than 500° C., in order to suppress the precipitation of coarse carbonitrides after working.
- a final heat treatment may be carried out.
- cold working may be added, if necessary, after the final heat treatment.
- Carbonitrides must be dissolved by heat treatment before the cold working. It is desirable to carry out the heat-treatment before the cold working at a temperature that is higher than the lowest temperature of the heating temperature before the hot working and the hot working finishing temperature.
- the cold working is preferably performed by applying strain of 10% or more, and two or more times cold workings may be subjected.
- the heat treatment for finished products is carried out at a temperature in a range of 1170 to 1300° C.
- the temperature is preferably higher than the finishing temperature of the hot working or the above-mentioned heat treatment before the cold working, by 10° C. or more.
- the steel of the present invention is not necessarily a grain-refined steel from the viewpoint of corrosion resistance. However, if the steel should be grain refined, the final heat treatment should be carried out at a temperature lower than the temperature of the hot working finishing or the temperature of the above-mentioned heat treatment before the cold working, by 10° C. or more.
- the products are preferably cooled at a cooling rate of 0.25° C./sec or more in order to suppress the precipitation of coarse carbonitrides.
- the heat treatment temperature and the cooling rate may be controlled so that an amount of unsolved Nb in the finally heat-treated product is in a range of “0.04 ⁇ Cu (mass %)” to “0.085 ⁇ Cu (mass %)” by use of a steel whose chemical composition is controlled from 0.05 to 0.2 for the content ratio of Nb to Cu, i.e., “Nb/Cu”.
- the steels of Nos. 1 to 38 are steels of the present invention and steels of A to O are comparative steels.
- Test pieces were prepared from the obtained ingots by the following methods. As test pieces for evaluating high temperature ductility, the above-mentioned ingots were hot-forged into steel plates, each having a thickness of 40 mm, and round bar tensile test pieces (diameter: 10 mm, length: 130 mm) were prepared by machining.
- the above-mentioned ingots were hot-forged into steel plates having a thickness of 15 mm. After softening heat treatment, the steel plates were cold-rolled to 10 mm thickness and were maintained at 1230° C. for 15 minutes. Then the plates were water-cooled and the round bar test pieces (diameter: 6 mm, gauge length: 30 mm) were prepared by machining the plates.
- V notch test pieces (width: 5 mm, height: 10 mm, length: 55 mm, notch: 2 mm) were prepared for evaluating their toughness. Two test pieces were prepared for each steel.
- the above-mentioned round bar tensile test pieces (diameter: 10 mm, length: 130 mm) were used. Each of the test pieces was heated at 1220° C. for three minutes. Thereafter, a high-speed tensile test of a strain rate of 5/sec was performed and a reduction of area was obtained from the rupture surface. It is known that there are no serious problems in hot working such as hot extrusion when the reduction of area is 60% or more at the above-mentioned temperature. Accordingly, the reduction area of 60% or more was set for a criterion of a good hot workability.
- the above-mentioned round bar test pieces (diameter: 6 mm, gauge length: 30 mm) were used. With respect to each of the test pieces, a creep rupture test was performed in the atmospheres of 750° C. and 800° C. and a rupture strength at 750° C. and for 10 5 h was obtained by the Larson-Miller parameter method. Further, regarding the creep rupture elongation, the above-mentioned round bar test pieces (diameter: 6 mm, gauge length: 30 mm) were used. With respect to each of the test pieces a creep rupture test, which applies a load of 130 MPa at 750° C. was performed to measure a rupture elongation.
- V notch test pieces (width: 5 mm, height: 10 mm, length: 55 mm, notch: 2 mm) made of materials aged at 800° C. for 3,000 hours were used. Each test piece was cooled to 0° C. for the Charpy impact test and the average of test results of these two test pieces was obtained as an impact value.
- the amounts of precipitates of the steels, according to the present invention were measured by sampling test pieces from parallel portions of the ruptured specimens of a creep test, which was performed under 130 MPa at 750° C., observing structures by magnification of 10,000, using a transmission electron microscope, and countering the number of the respective precipitates separated by an electron beam diffraction pattern. The observation of the structure was performed in five fields and the average was determined as the precipitation amount.
- comparative steels A to C are examples, in which P contents exceed the range specified by the formula (1).
- the chemical compositions, except for P, of the comparative steels A and B are the same as those of the steels 1 and 2 of the present invention, and the P content of the comparative steel C is substantially the same as that of the steel 2 of the present invention.
- their values of reduction of area and creep rupture elongation are low. Therefore the creep rupture ductility and hot workability of these comparative steels are insufficient.
- V contents of the comparative steels G, H and I are in a range lower than the range specified by the present invention.
- the chemical compositions, except for V are substantially the same as those of the steels 7 and 8 of the present invention, the creep rupture strengths were low level.
- the Charpy impact values of the comparative examples G and H are smaller than those of examples 7 and 8 of the present invention.
- the comparative steel I is a steel within the scope of the invention proposed in the afore-mentioned Publication of unexamined Patent Application No.2001-49400.
- any one of the Cu content, C content and N content is less than the range specified by the present invention.
- the other chemical compositions of these steels are substantially the same as those of the steels 10, 11 and 12 of the present invention, respectively.
- creep rupture strengths are inferior to those of the steels of the present invention.
- the steels 9 to 11 and steels 13 to 37 of the present invention which include at least one element of the first group and/or the second group, are further improved in the hot workability and creep rupture strength.
- the present invention it can be possible that hot workability, strength and toughness, during long periods of use at a high temperature, are remarkably improved in the austenitic stainless steel containing Cu, Nb and N.
- the austenitic stainless steel of the present invention as a heat resistant and pressure resistant member under a high temperature of 650° C. to 700° C. or higher, contributes to making a plant highly efficient. Additionally, since the steel can be manufactured at lower costs, it can be used in various fields.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Business, Economics & Management (AREA)
- Educational Administration (AREA)
- Educational Technology (AREA)
- Heat Treatment Of Steel (AREA)
- Catalysts (AREA)
Abstract
Description
-
- (a) In order to increase the creep strength, it is effective to use an austenitic stainless steel, in which Cu, Nb and N are added together, for the base material.
- (b) For a significant improvement of the creep rupture ductility and hot workability, particularly the high temperature ductility at 1200° C. or higher, it is effective to control P and O properly, in accordance with the Cu content.
- (c) It is effective to control the Al content, in accordance with the N content, for the improvement of creep strength.
- (d) Addition of V to the steel is effective in not only the improvement of creep strength but also in the improvement of toughness, after the steel is used at a high temperature, particularly at 800° C. or higher, for long period.
P≦1/(11×Cu) (1)
sol.Al≦0.4×N (2)
Mo+(W/2)≦5 (3)
O≦1/(60×Cu) (4)
P≦1/(11×Cu) (1)
sol.Al≦0.4×N (2)
O≦1/(60×Cu) (4)
Mo+(W/2)≦5 (3)
TABLE 1 | ||
Chemical Composition (mass %, the balance: Fe and Incidental Impurities) |
Up- | Up- | |||||||||||||||||
Upper | per | per | ||||||||||||||||
Steel | limit | limit | limit | |||||||||||||||
No. | C | Si | Mn | P | S | Cr | Ni | Cu | Nb | V | Al | N | O | the others | of P | of Al | of O | |
Steel | 1 | 0.059 | 0.39 | 1.17 | 0.015 | 0.002 | 24.80 | 24.80 | 3.30 | 0.42 | 0.07 | 0.008 | 0.21 | 0.003 | 0.028 | 0.084 | 0.005 | |
of This | 2 | 0.060 | 0.41 | 1.23 | 0.026 | 0.002 | 25.20 | 24.70 | 3.31 | 0.44 | 0.06 | 0.009 | 0.22 | 0.002 | 0.027 | 0.088 | 0.005 | |
Invention | 3 | 0.089 | 0.39 | 1.22 | 0.017 | 0.002 | 24.80 | 29.90 | 2.95 | 0.45 | 0.11 | 0.015 | 0.20 | 0.002 | 0.031 | 0.080 | 0.006 | |
4 | 0.093 | 0.38 | 1.27 | 0.016 | 0.002 | 24.70 | 29.70 | 2.92 | 0.41 | 0.12 | 0.017 | 0.23 | 0.005 | 0.031 | 0.092 | 0.006 | ||
5 | 0.126 | 0.37 | 1.27 | 0.017 | 0.002 | 24.20 | 38.60 | 3.03 | 0.34 | 0.25 | 0.013 | 0.10 | 0.003 | 0.030 | 0.040 | 0.006 | ||
6 | 0.130 | 0.39 | 1.20 | 0.018 | 0.003 | 25.10 | 38.80 | 2.98 | 0.33 | 0.27 | 0.033 | 0.09 | 0.004 | 0.031 | 0.036 | 0.006 | ||
7 | 0.066 | 0.39 | 0.41 | 0.016 | 0.003 | 23.30 | 19.60 | 2.82 | 0.44 | 0.04 | 0.011 | 0.19 | 0.005 | 0.032 | 0.076 | 0.006 | ||
8 | 0.074 | 0.42 | 0.42 | 0.013 | 0.003 | 23.60 | 19.90 | 2.79 | 0.45 | 0.82 | 0.010 | 0.20 | 0.005 | 0.033 | 0.080 | 0.006 | ||
9 | 0.070 | 0.46 | 0.38 | 0.014 | 0.0005 | 23.20 | 20.10 | 2.96 | 0.44 | 0.23 | 0.013 | 0.20 | 0.005 | 0.0041B, | 0.031 | 0.080 | 0.006 | |
0.0035Ca | ||||||||||||||||||
10 | 0.061 | 0.47 | 1.19 | 0.008 | 0.002 | 20.30 | 18.40 | 2.14 | 0.47 | 0.44 | 0.015 | 0.17 | 0.005 | 0.31Mo, | 0.042 | 0.068 | 0.008 | |
1.63W | ||||||||||||||||||
11 | 0.056 | 0.44 | 1.27 | 0.007 | 0.003 | 21.20 | 15.80 | 3.41 | 0.35 | 0.46 | 0.009 | 0.26 | 0.003 | 0.67Mo, | 0.027 | 0.106 | 0.005 | |
1.33W | ||||||||||||||||||
12 | 0.058 | 0.41 | 1.22 | 0.018 | 0.002 | 24.60 | 20.50 | 2.82 | 0.71 | 0.15 | 0.015 | 0.06 | 0.004 | 0.032 | 0.024 | 0.006 | ||
13 | 0.058 | 0.42 | 1.30 | 0.017 | 0.002 | 27.40 | 25.80 | 3.70 | 0.46 | 0.17 | 0.018 | 0.22 | 0.003 | 3.56Co | 0.025 | 0.088 | 0.005 | |
14 | 0.056 | 0.41 | 1.22 | 0.017 | 0.003 | 25.20 | 29.90 | 3.76 | 0.48 | 0.27 | 0.015 | 0.21 | 0.003 | 2.88Mo | 0.024 | 0.084 | 0.004 | |
15 | 0.059 | 0.43 | 1.28 | 0.016 | 0.002 | 24.40 | 35.30 | 3.80 | 0.44 | 0.22 | 0.025 | 0.18 | 0.002 | 3.25W | 0.024 | 0.072 | 0.004 | |
16 | 0.070 | 0.41 | 1.18 | 0.015 | 0.003 | 24.90 | 24.40 | 3.73 | 0.44 | 0.26 | 0.017 | 0.23 | 0.002 | 0.05Ti | 0.024 | 0.093 | 0.004 | |
17 | 0.061 | 0.44 | 1.18 | 0.017 | 0.002 | 24.90 | 25.90 | 3.84 | 0.45 | 0.16 | 0.014 | 0.24 | 0.003 | 0.0049B | 0.024 | 0.096 | 0.004 | |
18 | 0.057 | 0.44 | 1.17 | 0.016 | 0.003 | 24.60 | 20.00 | 3.75 | 0.47 | 0.23 | 0.018 | 0.26 | 0.003 | 0.03Zr | 0.024 | 0.104 | 0.004 | |
19 | 0.069 | 0.39 | 1.26 | 0.018 | 0.003 | 25.30 | 23.70 | 3.90 | 0.43 | 0.41 | 0.017 | 0.24 | 0.003 | 0.0038Mg | 0.023 | 0.094 | 0.004 | |
20 | 0.057 | 0.37 | 1.29 | 0.017 | 0.003 | 25.30 | 19.60 | 3.71 | 0.42 | 0.20 | 0.013 | 0.25 | 0.003 | 0.0029Ca | 0.025 | 0.102 | 0.004 | |
21 | 0.060 | 0.41 | 1.24 | 0.016 | 0.002 | 25.00 | 19.80 | 3.67 | 0.47 | 1.25 | 0.014 | 0.27 | 0.004 | 0.04Y | 0.025 | 0.106 | 0.005 | |
22 | 0.059 | 0.43 | 1.19 | 0.017 | 0.002 | 25.00 | 20.10 | 3.66 | 0.46 | 0.26 | 0.019 | 0.26 | 0.002 | 0.06La | 0.025 | 0.106 | 0.005 | |
23 | 0.057 | 0.41 | 2.16 | 0.017 | 0.002 | 24.90 | 19.60 | 3.63 | 0.42 | 0.27 | 0.014 | 0.24 | 0.003 | 0.02Ce | 0.025 | 0.096 | 0.005 | |
24 | 0.055 | 0.38 | 1.25 | 0.016 | 0.002 | 24.80 | 20.40 | 3.73 | 0.45 | 0.30 | 0.012 | 0.27 | 0.002 | 0.04Nd | 0.024 | 0.108 | 0.004 | |
25 | 0.031 | 0.50 | 1.19 | 0.015 | 0.002 | 25.50 | 21.80 | 3.69 | 0.42 | 0.31 | 0.014 | 0.26 | 0.003 | 0.08Sc | 0.025 | 0.104 | 0.005 | |
26 | 0.056 | 0.42 | 1.20 | 0.016 | 0.002 | 25.20 | 20.10 | 3.74 | 0.44 | 0.29 | 0.014 | 0.26 | 0.002 | 0.21Hf | 0.024 | 0.105 | 0.004 | |
Note: | ||||||||||||||||||
“Al” means “sol.Al”. | ||||||||||||||||||
Upper limits of P, Al and O are obtained from formulas (1), (2) and (3), respectively. |
TABLE 2 | |||
Steel | Chemical Composition (mass %, the balance: Fe and Incidental Impurities) |
No. | C | Si | Mn | P | S | Cr | Ni | Cu | Nb | V | Al | |
Steel of | 28 | 0.057 | 0.39 | 1.21 | 0.016 | 0.002 | 25.50 | 48.6 | 3.83 | 0.48 | 0.16 | 0.015 |
This Invention | 29 | 0.056 | 0.42 | 1.26 | 0.015 | 0.002 | 25.20 | 44.9 | 3.84 | 0.47 | 0.09 | 0.015 |
30 | 0.059 | 0.45 | 1.18 | 0.015 | 0.003 | 24.90 | 52.5 | 3.67 | 0.45 | 0.26 | 0.018 | |
31 | 0.062 | 0.41 | 1.05 | 0.016 | 0.002 | 24.80 | 40.3 | 3.66 | 0.38 | 0.21 | 0.016 | |
32 | 0.060 | 0.40 | 1.14 | 0.014 | 0.002 | 25.30 | 48.5 | 3.58 | 0.44 | 0.23 | 0.018 | |
33 | 0.059 | 0.42 | 1.17 | 0.014 | 0.002 | 25.10 | 29.8 | 3.73 | 0.44 | 0.18 | 0.016 | |
34 | 0.060 | 0.40 | 1.22 | 0.014 | 0.003 | 25.50 | 29.7 | 3.79 | 0.45 | 0.20 | 0.017 | |
35 | 0.059 | 0.36 | 1.13 | 0.015 | 0.003 | 25.50 | 25.0 | 3.78 | 0.46 | 0.18 | 0.013 | |
36 | 0.056 | 0.37 | 1.15 | 0.015 | 0.002 | 25.20 | 34.5 | 3.84 | 0.42 | 0.27 | 0.012 | |
37 | 0.061 | 0.40 | 1.21 | 0.013 | 0.002 | 24.70 | 31.7 | 3.90 | 0.45 | 0.26 | 0.016 | |
38 | 0.055 | — | 0.85 | 0.014 | 0.001 | 23.80 | 20.4 | 2.88 | 0.20 | 0.51 | 0.013 | |
Comparative | A | 0.062 | 0.42 | 1.13 | 0.030* | 0.002 | 24.90 | 25.0 | 3.24 | 0.43 | 0.07 | 0.012 |
Examples | B | 0.060 | 0.41 | 1.20 | 0.036* | 0.002 | 24.80 | 24.9 | 3.29 | 0.43 | 0.08 | 0.010 |
C | 0.061 | 0.38 | 1.21 | 0.023* | 0.002 | 25.20 | 25.0 | 4.66 | 0.43 | 0.07 | 0.008 | |
D | 0.121 | 0.41 | 1.20 | 0.015 | 0.003 | 25.10 | 38.7 | 3.02 | 0.36 | 0.30 | 0.038* | |
E | 0.122 | 0.37 | 1.21 | 0.016 | 0.002 | 25.20 | 38.5 | 3.10 | 0.31 | 0.27 | 0.055* | |
F | 0.129 | 0.38 | 1.20 | 0.018 | 0.002 | 25.10 | 38.6 | 3.05 | 0.35 | 0.28 | 0.031* | |
G | 0.069 | 0.38 | 0.40 | 0.014 | 0.003 | 22.50 | 20.0 | 3.01 | 0.44 | 0.01* | 0.011 | |
H | 0.072 | 0.41 | 0.41 | 0.014 | 0.003 | 23.20 | 19.6 | 2.94 | 0.45 | 0.0005* | 0.009 | |
I | 0.070 | 0.40 | 0.43 | 0.016 | 0.0004 | 22.80 | 19.8 | 3.02 | 0.46 | 0.0004* | 0.012 | |
J | 0.059 | 0.41 | 1.21 | 0.007 | 0.002 | 20.50 | 18.5 | 1.81* | 0.46 | 0.46 | 0.012 | |
K | 0.041* | 0.46 | 1.29 | 0.005 | 0.002 | 20.80 | 16.0 | 3.38 | 0.37 | 0.47 | 0.011 | |
L | 0.060 | 0.39 | 1.20 | 0.017 | 0.001 | 24.90 | 20.8 | 2.79 | 0.75 | 0.16 | 0.014 | |
Chemical Composition (mass %, the balance: Fe and Incidental Impurities) |
Steel | Upper | Upper | Upper | ||||
No. | N | O | the others | limit of P | limit of Al | limit of O | |
Steel of | 28 | 0.10 | 0.002 | 3.3Re | 0.024 | 0.040 | 0.004 |
This Invention | 29 | 0.13 | 0.002 | 1.49Ir | 0.024 | 0.052 | 0.004 |
30 | 0.08 | 0.002 | 1.13Pd | 0.025 | 0.032 | 0.005 | |
31 | 0.10 | 0.002 | 0.52Pt | 0.025 | 0.040 | 0.005 | |
32 | 0.07 | 0.002 | 2.10Ag | 0.025 | 0.028 | 0.005 | |
33 | 0.21 | 0.002 | 0.0039B, 1.38W | 0.024 | 0.084 | 0.004 | |
34 | 0.20 | 0.003 | 0.02Zr, 0.98W, 0.0035Ca | 0.024 | 0.080 | 0.004 | |
35 | 0.23 | 0.002 | 1.43Co, 0.15Nd | 0.024 | 0.092 | 0.004 | |
36 | 0.19 | 0.003 | 4.50W, 0.08Y | 0.024 | 0.076 | 0.004 | |
37 | 0.21 | 0.002 | 3.17Mo, 0.76Hf | 0.023 | 0.084 | 0.004 | |
38 | 0.18 | 0.002 | 0.032 | 0.072 | 0.006 | ||
Comparative | A | 0.22 | 0.003 | 0.028 | 0.088 | 0.005 | |
Examples | B | 0.20 | 0.003 | 0.028 | 0.080 | 0.005 | |
C | 0.21 | 0.002 | 0.020 | 0.084 | 0.004 | ||
D | 0.09 | 0.003 | 0.030 | 0.036 | 0.006 | ||
E | 0.10 | 0.004 | 0.029 | 0.040 | 0.005 | ||
F | 0.06 | 0.003 | 0.030 | 0.024 | 0.005 | ||
G | 0.21 | 0.003 | 0.030 | 0.084 | 0.006 | ||
H | 0.19 | 0.004 | 0.031 | 0.076 | 0.006 | ||
I | 0.21 | 0.005 | 0.0043B, 0.0040Ca | 0.030 | 0.084 | 0.006 | |
J | 0.18 | 0.004 | 0.35Mo, 1.70W | 0.050 | 0.072 | 0.009 | |
K | 0.25 | 0.003 | 0.70Mo, 1.39W | 0.027 | 0.100 | 0.005 | |
L | 0.04* | 0.004 | 0.033 | 0.016 | 0.006 | ||
Note: | |||||||
“Al” means “sol.Al”. | |||||||
Upper limits of P, Al and O are obtained from formulas (1), (2) and (3), respectively. | |||||||
“*” shows out of the range defined by the present invention. |
TABLE 3 | ||||||
Creep | Creep | Charpy | ||||
Amount of Precipitates | Reduction | Rupture | Rupture | Impact |
Steel | (Nb, V) CrN | V (C, N) | of Area | Strength | Elongation | Value | |
No. | (Number/μm2) | (Number/μm2) | (%) | (MPa) | (%) | (J/cm2) | |
Steel of This | 1 | 9 | 21 | 88.1 | 71.2 | 31.9 | — |
Invention | 2 | 10 | 24 | 70.4 | 71.0 | 27.1 | — |
3 | 13 | 48 | 90.1 | 73.1 | 33.6 | — | |
4 | 12 | 51 | 78.0 | 73.6 | 31.1 | — | |
5 | 6 | 25 | 82.5 | 75.1 | 30.9 | — | |
6 | 6 | 28 | 88.3 | 75.8 | 32.2 | — | |
7 | 9 | 22 | 85.2 | 70.2 | 34.0 | 88 | |
8 | 15 | 162 | 83.5 | 78.5 | 29.1 | 105 | |
9 | 9 | 71 | 95.1 | 79.5 | 31.9 | — | |
10 | 12 | 95 | 89.8 | 80.5 | 32.2 | — | |
11 | 14 | 108 | 93.2 | 80.2 | 35.3 | — | |
12 | 9 | 42 | 72.0 | 70.9 | 27.3 | — | |
13 | 12 | 56 | 84.9 | 80.4 | 32.9 | — | |
14 | 12 | 74 | 81.6 | 80.5 | 31.0 | — | |
15 | 10 | 48 | 79.5 | 81.1 | 26.8 | — | |
16 | 13 | 76 | 83.7 | 80.0 | 30.4 | — | |
17 | 12 | 60 | 80.7 | 79.8 | 28.4 | — | |
18 | 15 | 82 | 79.2 | 79.7 | 31.2 | — | |
19 | 13 | 102 | 92.1 | 75.1 | 24.7 | — | |
20 | 13 | 66 | 93.0 | 75.4 | 30.2 | — | |
21 | 21 | 268 | 90.8 | 78.8 | 27.7 | — | |
22 | 14 | 87 | 95.2 | 74.6 | 29.5 | — | |
23 | 13 | 74 | 90.1 | 74.9 | 31.8 | — | |
24 | 14 | 94 | 93.6 | 75.0 | 33.8 | — | |
25 | 14 | 80 | 92.6 | 75.1 | 29.1 | — | |
26 | 12 | 88 | 88.5 | 79.8 | 30.7 | — | |
27 | 9 | 44 | 78.1 | 80.2 | 26.9 | ||
TABLE 4 | |||
Amount of Precipitates |
(Nb, V) | Creep | Creep | Charpy | ||||
CrN | V (C, N) | Reduction | Rupture | Rupture | Impact | ||
Steel | (Number/ | (Number/ | of Area | Strength | Elongation | Value | |
No. | μm2) | μm2) | (%) | (MPa) | (%) | (J/cm2) | |
Steel of This | 28 | 7 | 17 | 75.5 | 80.5 | 27.0 | — |
Invention | 29 | 8 | 12 | 76.4 | 81.2 | 30.3 | — |
30 | 7 | 23 | 78.4 | 81.4 | 27.8 | — | |
31 | 8 | 14 | 77.2 | 80.5 | 28.6 | — | |
32 | 8 | 13 | 76.5 | 80.8 | 29.0 | — | |
33 | 11 | 51 | 84.1 | 80.1 | 31.7 | — | |
34 | 11 | 53 | 92.0 | 80.4 | 31.7 | — | |
35 | 12 | 61 | 93.5 | 80.2 | 29.6 | — | |
36 | 10 | 56 | 92.6 | 80.9 | 28.1 | — | |
37 | 12 | 68 | 84.9 | 80.4 | 31.3 | — | |
38 | 9 | 54 | 81.6 | 72.5 | 30.0 | — | |
Comparative | A | 11 | 34 | 55.6 | 71.4 | 9.0 | — |
Examples | B | 10 | 28 | 32.3 | 70.9 | 5.5 | — |
C | 10 | 29 | 51.3 | 72.5 | 7.0 | — | |
D | 7 | 35 | 88.7 | 68.4 | 32.8 | — | |
E | 7 | 25 | 90.9 | 66.2 | 32.0 | — | |
F | 6 | 22 | 91.2 | 67.5 | 31.9 | — | |
G | 4 | 3 | 86.6 | 63.1 | 30.4 | 51 | |
H | 3 | 2 | 84.8 | 61.7 | 31.4 | 40 | |
I | 3 | 2 | 94.2 | 62.8 | 35.5 | — | |
J | 12 | 85 | 91.0 | 68.0 | 32.3 | — | |
K | 10 | 51 | 91.1 | 69.8 | 36.0 | — | |
L | 3 | 5 | 75.7 | 66.8 | 25.9 | — | |
Claims (8)
P≦1/(11×Cu) (1)
sol.Al≦0.4×N (2)
P≦1/(11×Cu) (1)
sol.Al≦0.4×N (2)
Mo+(W/2)≦5 (3)
P≦1/(11×Cu) (1)
sol.Al≦0.4×N (2)
P≦1/(11×Cu) (1)
sol.Al≦0.4×N (2)
Mo+(W/2)≦5 (3)
O≦1/(60×Cu) (4)
O≦1/(60×Cu) (4)
O≦1/(60×Cu) (4)
O≦1/(60×Cu) (4)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003122494A JP3838216B2 (en) | 2003-04-25 | 2003-04-25 | Austenitic stainless steel |
JP2003-122494 | 2003-04-25 |
Publications (2)
Publication Number | Publication Date |
---|---|
US20040234408A1 US20040234408A1 (en) | 2004-11-25 |
US6918968B2 true US6918968B2 (en) | 2005-07-19 |
Family
ID=32959716
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/829,274 Expired - Lifetime US6918968B2 (en) | 2003-04-25 | 2004-04-22 | Austenitic stainless steel |
Country Status (8)
Country | Link |
---|---|
US (1) | US6918968B2 (en) |
EP (1) | EP1471158B1 (en) |
JP (1) | JP3838216B2 (en) |
KR (1) | KR100596660B1 (en) |
CN (1) | CN1268776C (en) |
CA (1) | CA2464856C (en) |
DE (1) | DE602004000140T2 (en) |
ES (1) | ES2250939T3 (en) |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20060243356A1 (en) * | 2005-02-02 | 2006-11-02 | Yuusuke Oikawa | Austenite-type stainless steel hot-rolling steel material with excellent corrosion resistance, proof-stress, and low-temperature toughness and production method thereof |
US20080107559A1 (en) * | 2005-04-11 | 2008-05-08 | Yoshitaka Nishiyama | Austenitic stainless steel |
US20100000281A1 (en) * | 2006-12-28 | 2010-01-07 | Naoya Hirase | Method for manufacturing seamless steel pipe made of high Cr-high Ni alloy steel |
US20100034689A1 (en) * | 2007-10-03 | 2010-02-11 | Hiroyuki Hirata | Austenitic stainless steel |
US20110067475A1 (en) * | 2008-06-13 | 2011-03-24 | Sumitomo Metal Industries, Ltd. | Process for Producing High-Alloy Seamless Tube |
US9347121B2 (en) | 2011-12-20 | 2016-05-24 | Ati Properties, Inc. | High strength, corrosion resistant austenitic alloys |
RU2635645C1 (en) * | 2017-03-20 | 2017-11-14 | Юлия Алексеевна Щепочкина | Steel |
RU2651069C1 (en) * | 2017-11-27 | 2018-04-18 | Юлия Алексеевна Щепочкина | Iron-based alloy |
US10174397B2 (en) | 2014-02-13 | 2019-01-08 | Vdm Metals International Gmbh | Titanium-free alloy |
Families Citing this family (83)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20040221929A1 (en) | 2003-05-09 | 2004-11-11 | Hebda John J. | Processing of titanium-aluminum-vanadium alloys and products made thereby |
US7837812B2 (en) | 2004-05-21 | 2010-11-23 | Ati Properties, Inc. | Metastable beta-titanium alloys and methods of processing the same by direct aging |
CN100577844C (en) * | 2005-04-04 | 2010-01-06 | 住友金属工业株式会社 | Austenitic stainless steel |
JP5218065B2 (en) | 2007-01-15 | 2013-06-26 | 新日鐵住金株式会社 | Austenitic stainless steel welded joints and austenitic stainless steel welded materials |
JP4946758B2 (en) * | 2007-09-28 | 2012-06-06 | 住友金属工業株式会社 | High temperature austenitic stainless steel with excellent workability after long-term use |
JP5463527B2 (en) * | 2008-12-18 | 2014-04-09 | 独立行政法人日本原子力研究開発機構 | Welding material made of austenitic stainless steel, stress corrosion cracking preventive maintenance method and intergranular corrosion preventive maintenance method using the same |
ES2351281B1 (en) * | 2009-02-03 | 2011-09-28 | Valeo Termico, S.A. | HEAT EXCHANGER FOR GASES, ESPECIALLY OF EXHAUST GASES OF AN ENGINE. |
KR101091863B1 (en) * | 2009-03-06 | 2011-12-12 | 포스코특수강 주식회사 | Stainless steel having excellent high temperature strength and manufacturing method for the same |
US10053758B2 (en) | 2010-01-22 | 2018-08-21 | Ati Properties Llc | Production of high strength titanium |
US9255316B2 (en) | 2010-07-19 | 2016-02-09 | Ati Properties, Inc. | Processing of α+β titanium alloys |
US9206497B2 (en) | 2010-09-15 | 2015-12-08 | Ati Properties, Inc. | Methods for processing titanium alloys |
US8613818B2 (en) | 2010-09-15 | 2013-12-24 | Ati Properties, Inc. | Processing routes for titanium and titanium alloys |
US10513755B2 (en) | 2010-09-23 | 2019-12-24 | Ati Properties Llc | High strength alpha/beta titanium alloy fasteners and fastener stock |
RU2446223C1 (en) * | 2010-10-18 | 2012-03-27 | Сергей Васильевич Афанасьев | Heat-resistant chrome-nickel alloy with austenitic structure |
CN102002643B (en) * | 2010-12-18 | 2012-06-27 | 莘县荣盛精密铸造有限公司 | Thermocouple protection tube resisting high temperature and corrosion and production method thereof |
CN102650023A (en) * | 2011-02-23 | 2012-08-29 | 宝山钢铁股份有限公司 | Cu-Fe-Ni-Cr austenite alloy for oil bushing |
JP5549628B2 (en) * | 2011-03-25 | 2014-07-16 | 新日鐵住金株式会社 | Erhardt drilling method |
WO2012132992A1 (en) | 2011-03-28 | 2012-10-04 | 住友金属工業株式会社 | High-strength austenitic stainless steel for high-pressure hydrogen gas |
US8652400B2 (en) | 2011-06-01 | 2014-02-18 | Ati Properties, Inc. | Thermo-mechanical processing of nickel-base alloys |
JP5661001B2 (en) * | 2011-08-23 | 2015-01-28 | 山陽特殊製鋼株式会社 | High strength austenitic heat resistant steel with excellent post-aging toughness |
RU2465359C1 (en) * | 2011-09-15 | 2012-10-27 | Российская Федерация в лице Министерства промышленности и торговли Российской Федерации (Минпромторг России) | Heat-resistant alloy on nickel basis for monocrystalline casting |
JP5794945B2 (en) | 2012-03-30 | 2015-10-14 | 新日鐵住金ステンレス株式会社 | Heat resistant austenitic stainless steel sheet |
DE102012014068B3 (en) * | 2012-07-13 | 2014-01-02 | Salzgitter Mannesmann Stainless Tubes GmbH | Austenitic steel alloy with excellent creep rupture strength and oxidation and corrosion resistance at elevated service temperatures |
US9050647B2 (en) | 2013-03-15 | 2015-06-09 | Ati Properties, Inc. | Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys |
CN109321822A (en) * | 2012-10-30 | 2019-02-12 | 株式会社神户制钢所 | Austenite stainless steel |
CN102951584B (en) * | 2012-11-20 | 2015-09-16 | 江苏高博智融科技有限公司 | A kind of electromagnetic induction capper |
US9869003B2 (en) | 2013-02-26 | 2018-01-16 | Ati Properties Llc | Methods for processing alloys |
US9192981B2 (en) | 2013-03-11 | 2015-11-24 | Ati Properties, Inc. | Thermomechanical processing of high strength non-magnetic corrosion resistant material |
US9777361B2 (en) | 2013-03-15 | 2017-10-03 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
CN103266286A (en) * | 2013-06-14 | 2013-08-28 | 兰州理工大学 | High-alumina 316L stainless steel and preparation method thereof |
RU2543587C2 (en) * | 2013-07-09 | 2015-03-10 | Федеральное Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Конструкционных Материалов "Прометей" (Фгуп "Цнии Км "Прометей") | Heat resistant alloy on nickel base |
CN103409697B (en) * | 2013-07-30 | 2016-01-20 | 青岛新力通工业有限责任公司 | Novel resistance to aluminium, zine corrosion nichrome and adopt the method for this alloy production furnace roller |
US11111552B2 (en) | 2013-11-12 | 2021-09-07 | Ati Properties Llc | Methods for processing metal alloys |
CN103695806B (en) * | 2013-12-10 | 2016-08-17 | 江苏武进不锈股份有限公司 | A kind of austenitic heat-resistance steel |
CN104197105A (en) * | 2014-08-28 | 2014-12-10 | 安徽中臣机电装备科技有限公司 | Stainless steel pipe |
CN104264045B (en) * | 2014-09-01 | 2017-05-10 | 宝鸡石油钢管有限责任公司 | Steel for heat-resistant high-strength sleeve and preparation process of steel |
CN104195460B (en) * | 2014-09-02 | 2016-08-17 | 江苏武进不锈股份有限公司 | Austenitic heat-resistance steel |
CN104338335B (en) * | 2014-09-19 | 2016-04-13 | 常熟市联明化工设备有限公司 | The explosion-proof alembic of chemical industry equipment |
CN107075629B (en) * | 2014-09-19 | 2020-03-24 | 日本制铁株式会社 | Austenitic stainless steel sheet |
CN104451447B (en) * | 2014-12-10 | 2016-10-19 | 无锡鑫常钢管有限责任公司 | A kind of Austenitic stainless steel pipe and production technology |
RU2563569C1 (en) * | 2014-12-22 | 2015-09-20 | Юлия Алексеевна Щепочкина | Steel |
US10094003B2 (en) | 2015-01-12 | 2018-10-09 | Ati Properties Llc | Titanium alloy |
KR101965524B1 (en) | 2015-03-06 | 2019-04-03 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | High strength austenitic stainless steel excellent in hydrogen embrittlement resistance and manufacturing method thereof |
CN104694783B (en) * | 2015-03-13 | 2017-07-07 | 江苏申源特钢有限公司 | A kind of nickel-based gas valve alloy and preparation method thereof |
JP6684620B2 (en) * | 2015-03-26 | 2020-04-22 | 日鉄ステンレス株式会社 | High-strength austenitic stainless steel excellent in hydrogen embrittlement resistance, its manufacturing method, and hydrogen equipment used in high-pressure hydrogen gas and liquid hydrogen environment |
US11149324B2 (en) | 2015-03-26 | 2021-10-19 | Nippon Steel Stainless Steel Corporation | High strength austenitic stainless steel having excellent resistance to hydrogen embrittlement, method for manufacturing the same, and hydrogen equipment used for high-pressure hydrogen gas and liquid hydrogen environment |
RU2581323C1 (en) * | 2015-06-01 | 2016-04-20 | Байдуганов Александр Меркурьевич | High-temperature alloy |
ES2788648T3 (en) * | 2015-06-15 | 2020-10-22 | Nippon Steel Corp | Austenitic stainless steel based on high Cr content |
JP2017014576A (en) * | 2015-07-01 | 2017-01-19 | 新日鐵住金株式会社 | Austenitic heat resistant alloy and weldment structure |
JP6547599B2 (en) * | 2015-11-10 | 2019-07-24 | 日本製鉄株式会社 | Austenitic heat resistant steel |
US10502252B2 (en) | 2015-11-23 | 2019-12-10 | Ati Properties Llc | Processing of alpha-beta titanium alloys |
RU2609155C1 (en) * | 2015-12-07 | 2017-01-30 | Юлия Алексеевна Щепочкина | Steel |
JP6955322B2 (en) * | 2016-03-15 | 2021-10-27 | 山陽特殊製鋼株式会社 | Austenitic heat-resistant steel with excellent workability, high-temperature strength and toughness after aging |
CN106119721A (en) * | 2016-07-29 | 2016-11-16 | 安庆市德奥特汽车零部件制造有限公司 | A kind of preparation method of ageing-resistant composite coating piston ring for combustion engines |
CN106077662A (en) * | 2016-07-29 | 2016-11-09 | 安庆市德奥特汽车零部件制造有限公司 | A kind of preparation method of high temperature resistant composite coating piston ring for combustion engines |
CN107326287A (en) * | 2017-06-09 | 2017-11-07 | 太仓东旭精密机械有限公司 | A kind of component of machine steel |
CN107639584A (en) * | 2017-09-14 | 2018-01-30 | 国家电网公司 | Combined electrical apparatus disintegration Special assisting tool |
CN107571188A (en) * | 2017-09-14 | 2018-01-12 | 国家电网公司 | Combined electrical apparatus disintegration Special assisting tool |
CN107858589A (en) * | 2017-09-20 | 2018-03-30 | 常州凯旺金属材料有限公司 | The stainless iron and heat treatment method of a kind of corrosion-and high-temp-resistant |
CN111344427B (en) | 2017-11-15 | 2021-08-31 | 日本制铁株式会社 | Austenitic heat-resistant steel weld metal, weld joint, weld material for austenitic heat-resistant steel, and method for producing weld joint |
CN108220801A (en) * | 2018-01-08 | 2018-06-29 | 浙江华鸣不锈钢有限公司 | A kind of Austenitic stainless steel pipe and its preparation process |
CA3086462C (en) * | 2018-01-26 | 2022-06-14 | Nippon Steel Corporation | Cr-ni alloy and seamless steel pipe made of cr-ni alloy |
RU2663954C1 (en) * | 2018-02-13 | 2018-08-13 | Юлия Алексеевна Щепочкина | Iron-based alloy |
JP6999479B2 (en) * | 2018-04-05 | 2022-02-04 | 日鉄ステンレス株式会社 | Complete austenitic stainless steel |
CN108411208A (en) * | 2018-04-11 | 2018-08-17 | 石英楠 | A kind of preparation method of power plants generating electricity unit austenite heat-resistance stainless steel |
RU2683173C1 (en) * | 2018-05-31 | 2019-03-26 | Акционерное общество "Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения", АО "НПО "ЦНИИТМАШ" | High-strength nonmagnetic corrosion-resistant steel |
CN109023011A (en) * | 2018-07-27 | 2018-12-18 | 含山县林宏铸造厂 | A kind of stainless steel metal plate resistant to high temperature |
CN109047798B (en) * | 2018-08-06 | 2020-06-23 | 宁波市鄞州兴韩机械实业有限公司 | Mechanical main shaft and preparation method thereof |
CN108950403B (en) * | 2018-08-13 | 2020-07-03 | 广东省材料与加工研究所 | Alloy steel and preparation method thereof |
US11692232B2 (en) | 2018-09-05 | 2023-07-04 | Gregory Vartanov | High strength precipitation hardening stainless steel alloy and article made therefrom |
CN109355594B (en) * | 2018-12-22 | 2022-04-01 | 佛山培根细胞新材料有限公司 | Copper-vanadium-cobalt modified stainless steel and processing and heat treatment method thereof |
CN111826621A (en) * | 2019-04-17 | 2020-10-27 | 中国兵器工业第五九研究所 | Glass mould pressing coating and preparation method and application thereof |
RU2700347C1 (en) * | 2019-06-13 | 2019-09-16 | Сергей Васильевич Афанасьев | Heat-resistant alloy |
CN112760553A (en) * | 2019-10-21 | 2021-05-07 | 宝山钢铁股份有限公司 | Super austenitic heat-resistant steel, seamless pipe and manufacturing method thereof |
JP7360032B2 (en) * | 2019-11-15 | 2023-10-12 | 日本製鉄株式会社 | Austenitic heat resistant steel welded joints |
CN111455161B (en) * | 2020-04-08 | 2021-11-16 | 山西太钢不锈钢股份有限公司 | Method for regulating and controlling structure performance of austenitic heat-resistant stainless steel seamless tube |
CN112375958A (en) * | 2020-10-28 | 2021-02-19 | 滦县天时矿山机械设备有限公司 | Preparation process of high-strength and high-toughness rare earth wear-resistant steel by rare earth treatment and pure smelting |
CN115323287A (en) * | 2022-06-23 | 2022-11-11 | 南宁龙鸣新能源有限公司 | Thin-wall titanium-silver metal material and manufacturing method thereof |
CN115537604B (en) * | 2022-09-23 | 2023-10-20 | 北京北冶功能材料有限公司 | Creep-resistant and oxidation-resistant nickel-based superalloy, and preparation method and application thereof |
CN115772636A (en) * | 2022-11-23 | 2023-03-10 | 江苏安宇捷热工科技有限公司 | High-temperature wear-resistant corrosion-resistant alloy |
CN115807191B (en) * | 2022-12-01 | 2024-03-12 | 振石集团华智研究院(浙江)有限公司 | Stainless steel material and preparation method thereof |
CN116005074B (en) * | 2023-01-30 | 2023-06-16 | 宁波市鄞州鑫旺热镀锌有限公司 | Hot dip galvanized steel sheet and preparation method thereof |
CN116657019B (en) * | 2023-07-26 | 2023-10-03 | 内蒙古工业大学 | NiTiAlVCMo powder-based laser additive alloy, composite coating and preparation method of composite coating |
Citations (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61183452A (en) * | 1985-02-09 | 1986-08-16 | Sumitomo Metal Ind Ltd | High manganese steel having resistance to corrosion at high temperature under stuck caso4 |
US4742324A (en) | 1984-04-27 | 1988-05-03 | Sumitomo Metal Industries Ltd. | Sheath heater |
JPS63309392A (en) | 1987-06-11 | 1988-12-16 | Nippon Steel Corp | Filler material for tig welding for austenitic heat resistant alloy |
US4842823A (en) | 1985-01-10 | 1989-06-27 | Sumitomo Metal Industries, Ltd. | Austenitic steel having improved high-temperature strength and corrosion resistance |
JPH01287249A (en) * | 1988-12-27 | 1989-11-17 | Nkk Corp | Austenitic stainless steel tube and its manufacture |
US5378427A (en) | 1991-03-13 | 1995-01-03 | Sumitomo Metal Industries, Ltd. | Corrosion-resistant alloy heat transfer tubes for heat-recovery boilers |
JPH07138708A (en) | 1993-11-18 | 1995-05-30 | Sumitomo Metal Ind Ltd | Austenitic steel good in high temperature strength and hot workability |
EP0690141A1 (en) | 1994-06-28 | 1996-01-03 | Sumitomo Chemical Company, Limited | An austenitic heat resistant steel excellent in elevated temperature strength |
JPH0830247A (en) | 1994-07-20 | 1996-02-02 | Fujitsu General Ltd | Display device |
EP0780483A1 (en) | 1995-12-20 | 1997-06-25 | Nippon Steel Corporation | High-strength austenitic heat-resisting steel having improved weldability |
JPH09195005A (en) | 1996-01-10 | 1997-07-29 | Sumitomo Metal Ind Ltd | Austenitic heat resistant steel excellent in high temperature strength |
JP2000073145A (en) | 1998-08-26 | 2000-03-07 | Sumitomo Metal Ind Ltd | Austenitic stainless steel excellent in hot workability |
JP2000328198A (en) | 1999-05-11 | 2000-11-28 | Sumitomo Metal Ind Ltd | Austenitic stainless steel excellent in hot workability |
JP2001049400A (en) | 1999-08-06 | 2001-02-20 | Sumitomo Metal Ind Ltd | Austenitic heat resisting steel excellent in hot workability |
JP2001107196A (en) * | 1999-10-07 | 2001-04-17 | Sumitomo Metal Ind Ltd | Austenitic steel welded joint excellent in weld cracking resistance and sulfuric acid corrosion resistance and the welding material |
JP2002212634A (en) | 2000-11-17 | 2002-07-31 | Nippon Steel Corp | Method for producing austenitic heat resistant steel tue having excellent creep rupture strength |
US6485679B1 (en) | 1999-02-16 | 2002-11-26 | Sandvik Ab | Heat resistant austenitic stainless steel |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100418973B1 (en) * | 2000-12-18 | 2004-02-14 | 김영식 | Low Mo bearing austenitic stainless steels with high pitting corrosion resistance |
JP3632672B2 (en) * | 2002-03-08 | 2005-03-23 | 住友金属工業株式会社 | Austenitic stainless steel pipe excellent in steam oxidation resistance and manufacturing method thereof |
-
2003
- 2003-04-25 JP JP2003122494A patent/JP3838216B2/en not_active Expired - Fee Related
-
2004
- 2004-04-06 KR KR1020040023307A patent/KR100596660B1/en active IP Right Grant
- 2004-04-22 ES ES04009588T patent/ES2250939T3/en not_active Expired - Lifetime
- 2004-04-22 DE DE602004000140T patent/DE602004000140T2/en not_active Expired - Lifetime
- 2004-04-22 EP EP04009588A patent/EP1471158B1/en not_active Expired - Fee Related
- 2004-04-22 US US10/829,274 patent/US6918968B2/en not_active Expired - Lifetime
- 2004-04-23 CN CNB2004100351150A patent/CN1268776C/en not_active Expired - Fee Related
- 2004-04-23 CA CA002464856A patent/CA2464856C/en not_active Expired - Fee Related
Patent Citations (18)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4742324A (en) | 1984-04-27 | 1988-05-03 | Sumitomo Metal Industries Ltd. | Sheath heater |
US4842823A (en) | 1985-01-10 | 1989-06-27 | Sumitomo Metal Industries, Ltd. | Austenitic steel having improved high-temperature strength and corrosion resistance |
JPS61183452A (en) * | 1985-02-09 | 1986-08-16 | Sumitomo Metal Ind Ltd | High manganese steel having resistance to corrosion at high temperature under stuck caso4 |
JPS63309392A (en) | 1987-06-11 | 1988-12-16 | Nippon Steel Corp | Filler material for tig welding for austenitic heat resistant alloy |
JPH01287249A (en) * | 1988-12-27 | 1989-11-17 | Nkk Corp | Austenitic stainless steel tube and its manufacture |
US5378427A (en) | 1991-03-13 | 1995-01-03 | Sumitomo Metal Industries, Ltd. | Corrosion-resistant alloy heat transfer tubes for heat-recovery boilers |
JPH07138708A (en) | 1993-11-18 | 1995-05-30 | Sumitomo Metal Ind Ltd | Austenitic steel good in high temperature strength and hot workability |
JPH0813102A (en) | 1994-06-28 | 1996-01-16 | Sumitomo Metal Ind Ltd | Austenitic heat resistant steel excellent in high temperature strength |
EP0690141A1 (en) | 1994-06-28 | 1996-01-03 | Sumitomo Chemical Company, Limited | An austenitic heat resistant steel excellent in elevated temperature strength |
JPH0830247A (en) | 1994-07-20 | 1996-02-02 | Fujitsu General Ltd | Display device |
EP0780483A1 (en) | 1995-12-20 | 1997-06-25 | Nippon Steel Corporation | High-strength austenitic heat-resisting steel having improved weldability |
JPH09195005A (en) | 1996-01-10 | 1997-07-29 | Sumitomo Metal Ind Ltd | Austenitic heat resistant steel excellent in high temperature strength |
JP2000073145A (en) | 1998-08-26 | 2000-03-07 | Sumitomo Metal Ind Ltd | Austenitic stainless steel excellent in hot workability |
US6485679B1 (en) | 1999-02-16 | 2002-11-26 | Sandvik Ab | Heat resistant austenitic stainless steel |
JP2000328198A (en) | 1999-05-11 | 2000-11-28 | Sumitomo Metal Ind Ltd | Austenitic stainless steel excellent in hot workability |
JP2001049400A (en) | 1999-08-06 | 2001-02-20 | Sumitomo Metal Ind Ltd | Austenitic heat resisting steel excellent in hot workability |
JP2001107196A (en) * | 1999-10-07 | 2001-04-17 | Sumitomo Metal Ind Ltd | Austenitic steel welded joint excellent in weld cracking resistance and sulfuric acid corrosion resistance and the welding material |
JP2002212634A (en) | 2000-11-17 | 2002-07-31 | Nippon Steel Corp | Method for producing austenitic heat resistant steel tue having excellent creep rupture strength |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20120111457A1 (en) * | 2005-02-02 | 2012-05-10 | Nippon Steel Corporation | Austenite-type stainless steel hot-rolling steel material with excellent corrosion resistance, proof-stress, and low-temperature toughness and production method thereof |
US8506729B2 (en) * | 2005-02-02 | 2013-08-13 | Nippon Steel & Sumikin Stainless Steel Corporation | Austenite-type stainless steel hot-rolling steel material with excellent corrosion resistance, proof-stress, and low-temperature toughness and production method thereof |
US8105447B2 (en) | 2005-02-02 | 2012-01-31 | Nippon Steel & Sumikin Stainless Steel Corporation | Austenitic stainless hot-rolled steel material with excellent corrosion resistance, proof stress, and low-temperature toughness |
US20100230011A1 (en) * | 2005-02-02 | 2010-09-16 | Nippon Steel & Sumikin Stainless Steel Corporation | Austenite-type stainless steel hot-rolling steel material with excellent corrosion resistance, proof-stress, and low-temperature toughness and production method thereof |
US20060243356A1 (en) * | 2005-02-02 | 2006-11-02 | Yuusuke Oikawa | Austenite-type stainless steel hot-rolling steel material with excellent corrosion resistance, proof-stress, and low-temperature toughness and production method thereof |
US20080107559A1 (en) * | 2005-04-11 | 2008-05-08 | Yoshitaka Nishiyama | Austenitic stainless steel |
US9150947B2 (en) * | 2005-04-11 | 2015-10-06 | Nippon Steel & Sumitomo Metal Corporation | Austenitic stainless steel |
US7866199B2 (en) * | 2006-12-28 | 2011-01-11 | Sumitomo Metal Industries, Ltd. | Method for manufacturing seamless steel pipe made of high Cr-high Ni alloy steel |
US20100000281A1 (en) * | 2006-12-28 | 2010-01-07 | Naoya Hirase | Method for manufacturing seamless steel pipe made of high Cr-high Ni alloy steel |
US20100034689A1 (en) * | 2007-10-03 | 2010-02-11 | Hiroyuki Hirata | Austenitic stainless steel |
US20110067475A1 (en) * | 2008-06-13 | 2011-03-24 | Sumitomo Metal Industries, Ltd. | Process for Producing High-Alloy Seamless Tube |
US8245552B2 (en) * | 2008-06-13 | 2012-08-21 | Sumitomo Metal Industries, Ltd. | Process for producing high-alloy seamless tube |
US9347121B2 (en) | 2011-12-20 | 2016-05-24 | Ati Properties, Inc. | High strength, corrosion resistant austenitic alloys |
US10174397B2 (en) | 2014-02-13 | 2019-01-08 | Vdm Metals International Gmbh | Titanium-free alloy |
RU2635645C1 (en) * | 2017-03-20 | 2017-11-14 | Юлия Алексеевна Щепочкина | Steel |
RU2651069C1 (en) * | 2017-11-27 | 2018-04-18 | Юлия Алексеевна Щепочкина | Iron-based alloy |
Also Published As
Publication number | Publication date |
---|---|
ES2250939T3 (en) | 2006-04-16 |
CN1540026A (en) | 2004-10-27 |
KR100596660B1 (en) | 2006-07-03 |
EP1471158B1 (en) | 2005-10-19 |
CN1268776C (en) | 2006-08-09 |
DE602004000140D1 (en) | 2006-03-02 |
EP1471158A1 (en) | 2004-10-27 |
JP2004323937A (en) | 2004-11-18 |
CA2464856A1 (en) | 2004-10-25 |
KR20040092410A (en) | 2004-11-03 |
DE602004000140T2 (en) | 2006-07-06 |
CA2464856C (en) | 2007-08-21 |
JP3838216B2 (en) | 2006-10-25 |
US20040234408A1 (en) | 2004-11-25 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US6918968B2 (en) | Austenitic stainless steel | |
US7731895B2 (en) | Austenitic Fe-Ni-Cr alloy | |
EP1445342B1 (en) | Austenitic stainless steel and manufacturing method thereof | |
JP4431905B2 (en) | Austenitic heat-resistant alloy, heat-resistant pressure-resistant member made of this alloy, and manufacturing method thereof | |
US6926778B2 (en) | Austenitic stainless steel excellent in high temperature strength and corrosion resistance, heat resistant pressurized parts, and the manufacturing method thereof | |
JP5794945B2 (en) | Heat resistant austenitic stainless steel sheet | |
US7507306B2 (en) | Precipitation-strengthened nickel-iron-chromium alloy and process therefor | |
US6358336B1 (en) | Heat resistance Cr-Mo alloy steel | |
US20090123322A1 (en) | High-Speed Steel for Saw Blades | |
JP5838933B2 (en) | Austenitic heat resistant steel | |
JP6547599B2 (en) | Austenitic heat resistant steel | |
RU2383649C2 (en) | Precipitation hardening steel (versions) and item out of steel (versions) | |
JP2019151920A (en) | HIGH Mn STEEL AND MANUFACTURING METHOD THEREFOR | |
JP2015147975A (en) | Precipitation hardening stainless steel and component for sensor | |
JP3848463B2 (en) | High strength austenitic heat resistant steel with excellent weldability and method for producing the same | |
JP2000204434A (en) | Ferritic heat resistant steel excellent in high temperature strength and its production | |
JP2890073B2 (en) | High Nb-containing high nitrogen ferritic heat-resistant steel and method for producing the same | |
RU76647U1 (en) | SHAFT (OPTIONS) | |
WO2019168172A1 (en) | HIGH Mn STEEL AND METHOD FOR PRODUCING SAME | |
JPH11106860A (en) | Ferritic heat resistant steel excellent in creep characteristic in heat-affected zone | |
JPH05179378A (en) | Ni-base alloy excellent in room temperature and high temperature strength | |
KR100268708B1 (en) | Method of manufacturing high cr ferritic heat resisting steel for high temperature,high pressure parts | |
JP2004124188A (en) | HIGH Cr HEAT-RESISTANT STEEL AND METHOD FOR MANUFACTURING THE SAME | |
JP7348553B2 (en) | oil country tubing | |
JP2021113354A (en) | Austenitic stainless steel |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: SUMITOMO METAL INDUSTRIES, LTD., JAPAN Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:SEMBA, HIROYUKI;IGARASHI, MASAAKI;REEL/FRAME:015261/0351;SIGNING DATES FROM 20040408 TO 20040413 |
|
STCF | Information on status: patent grant |
Free format text: PATENTED CASE |
|
FPAY | Fee payment |
Year of fee payment: 4 |
|
FPAY | Fee payment |
Year of fee payment: 8 |
|
FPAY | Fee payment |
Year of fee payment: 12 |
|
AS | Assignment |
Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION, JAPAN Free format text: MERGER;ASSIGNOR:SUMITOMO METAL INDUSTRIES, LTD.;REEL/FRAME:049165/0517 Effective date: 20121003 Owner name: NIPPON STEEL CORPORATION, JAPAN Free format text: CHANGE OF NAME;ASSIGNOR:NIPPON STEEL & SUMITOMO METAL CORPORATION;REEL/FRAME:049257/0828 Effective date: 20190401 |